EP1042516A1 - Cold drawn wire and method for the manufacturing of such wire - Google Patents
Cold drawn wire and method for the manufacturing of such wireInfo
- Publication number
- EP1042516A1 EP1042516A1 EP98963686A EP98963686A EP1042516A1 EP 1042516 A1 EP1042516 A1 EP 1042516A1 EP 98963686 A EP98963686 A EP 98963686A EP 98963686 A EP98963686 A EP 98963686A EP 1042516 A1 EP1042516 A1 EP 1042516A1
- Authority
- EP
- European Patent Office
- Prior art keywords
- max
- slag
- wire
- esr
- cold drawn
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/52—Manufacture of steel in electric furnaces
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/02—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for springs
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C5/00—Manufacture of carbon-steel, e.g. plain mild steel, medium carbon steel or cast steel or stainless steel
- C21C5/005—Manufacture of stainless steel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/06—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires
- C21D8/065—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of rods or wires of ferrous alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22B—PRODUCTION AND REFINING OF METALS; PRETREATMENT OF RAW MATERIALS
- C22B9/00—General processes of refining or remelting of metals; Apparatus for electroslag or arc remelting of metals
- C22B9/16—Remelting metals
- C22B9/18—Electroslag remelting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D6/00—Heat treatment of ferrous alloys
- C21D6/02—Hardening by precipitation
Definitions
- the invention relates to a method for the manufacture of a cold drawn wire of a precipitation hardenable stainless steel.
- the invention also relates to the cold drawn wire and to precipitation hardened springs made of the cold drawn wire.
- the stainless steel in the springs consists of so called 17-7 PH steel.
- the fatigue resistance to a high degree depends on the surface of the spring wire.
- the wire In order that the spring shall have a high fatigue resistance, the wire must not have any visible defects, which can initiate fatigue failures.
- the surface layer contain any large slag inclusions or large zones containing major accumulations of smaller slag inclusions, which also can initiate failures.
- ESR Electro Slag Refining
- a conventional slag mixture which is used according to known technique, and which at the ESR remelting process forms a melt, in which the electrode that shall be remelted is molten off drop- wise, such that the drops will sink through the slag melt to an underlying pond of molten metal, which solidifies successively to form a new ingot.
- a slag mixture can be used, which is known per se, and which contains appr 30 % of each of CaF 2 , CaO, and Al 2 O 3 and normally a certain amount of MgO in lime fraction as well as one or a few percent SiO 2 .
- the melting electrode as according to the invention, consists of a stainless 17-7 PH steel, which contains slag inclusions of varying sizes
- the remelted ingot will get a different slag picture than before the remelting operation.
- the ESR slag functions as a screen for larger slag particles existing in the steel prior to the remelting operation. At least this appears to be true for those slags which have proved to have a detrimental effect on the fatigue strength of the spring wire, namely slags of type CaO, Al 2 O 3 , and MgO.
- the amount of smaller slag inclusions of this type in the remelted material is influenced only to a low degree.
- the fatigue tests which have been performed with conventional materials and with materials according to the invention show that the critical slag size limit lies between 20 and 30 ⁇ m. Therefore, slag inclusions larger than 30 ⁇ m shall be avoided.
- the wires should not contain slag particles larger than 25 ⁇ m.
- the steel that is used according to the invention may have a chemical composition which is well known in the art and which as a matter of fact is standardised since long (SIS 2388).
- the method of the invention for the manufacture of a cold drawn wire of a precipitation hardenable stainless steel comprises the following steps: - preparation of a melt, which besides iron contains in weight-%
- ESR ingots electro slag refining said ingot or cut-up strand, possibly after forging and/or rolling to the shape of electrodes suitable for electro slag refining, to form ESR ingots; - hot working said ESR ingots, said hot working being finished by wire rolling, followed by pickling for the formation of a pickled, rolled wire, which in a surface layer thereof, to the depth of 1 mm counted from the surface, in a longitudinal, central section through the wire, does not contain slag inclusions larger than 30 ⁇ m, preferably max 25 ⁇ m; and - cold drawing the wire with at least 30 % reduction.
- Al is added as a subsequent operation, when the molten metal has got its intended basic composition through conventional steel manufacturing practice, suitably in a ladle treatment process which follows subsequent to decarburisation in a converter.
- the invention relates to the manufacture of a precipitation hardenable stainless steel according to the method that is described in the foregoing, which steel besides iron contains in weight-%: 0.3-0.1 , preferably max. 0.09 C
- Helicoidal springs are spun in a conventional mode of the cold drawn wire according to the invention.
- the springs are precipitation hardened through heat treatment at a temperature of 450-500°C for 0.5-2 h, suitably at appr 480°C for 1 h. followed by cooling in air.
- the structure of the material in the finished springs consists of 50-70 volume-% tempered martensite containing precipitated phases of aluminium and nickel in the martensite, preferably AlNi 3 , remainder austenite and max 5 % ⁇ -ferrite.
- This melt was cast to the form of a strand having the cross section 300 x 400 mm.
- the strand was cut up to blooms. A number of these blooms were rolled to the size 265-300 mm and were used as electrodes for subsequent ESR remelting. The remaining blooms were hot rolled to form rods with 150 mm square section, which rods were surface ground, hot rolled to the shape of wire with the 0 5.5 mm, and pickled.
- the ESR melting was carried out in a conventional way in a slag melt consisting of appr. 30 % of each of CaF 2 , CaO, and Al 2 O 3 . Also a certain amount of MgO was present in the lime fraction. The slag also contained a minor amount of SiO 2 . Through remelting of the electrodes in this slag, there was formed an ESR ingot (ESR-heat 14484) with the following composition in weight-%
- the composition of the steel was influenced to a certain degree. This particularly concerned the content of aluminium, which was reduced significantly, which indicates that aluminium ought to be added in connection with the ESR remelting in order to compensate for the losses. This can be carried out by means of an aluminium wire, which is caused to melt off in the melting pond beneath the slag layer.
- Rods with 150 mm square section were manufactured through hot working from the ESR ingot.
- the rods were ground and hot rolled to wires with the size 0 5.5 mm.
- the rolled wires were pickled and samples were taken out for slag examination.
- Oxidic slag inclusions (particles) which could be discovered in the light-optical microscope were notified as well as the existance of any bands or zones containing larger accumulations of slag inclusions.
- the slag inclusions were classified in three size groups, A, B, and C, for small slag inclusions (5-10 ⁇ m), medium size slag inclusions (> 10- 15 ⁇ m), and large slag inclusions (>15 ⁇ m). Further, the number of zones of slag inclusions were notified, the length of such zones, and the type of size of the slag inclusions in these zones.
- Table 1 where materials la w and lb w are rolled wire material manufactured in the conventional manner starting from the above mentioned heat No.
- the materials 2a w and 3a w were non approvable as materials for springs for injections pumps for Diesel engines as distinguished from the materials 2b w and 3b w , which did not contain any large slag inclusions in the surface layers and no or only some minor zone containing small accumulations of small slag inclusions.
- All the slag inclusions that have been discussed above consisted of CaO, Al 2 O 3j and MgO. Also Ti-nitrides were observed but were not entered in the slag protocols. These Ti-nitrides eminate from a pratice during the steel manufacturing process, in which titanium is added in order to prevent the formation of large, oxidic inclusions. The small Ti-nitrides, which are formed because of this practice, have been regarded as harmless. However, they have pronouncedly angular shape and it is therefore a potential risk that they can initiate fatigue failures. Therefore, titanium should be added to the melt, especially as the large slag inclusions have proved to be effectively eliminated by the ESR refining. Preferably, therefore, one should prepare a bulk of molten metal which does not contain titanium in amounts exceeding impurity level.
- intermetallic phases of aluminium and nickel were precipitated, typically AlNi 3 , in the martensite in a way which is typical for 17-7 PH steels, causing the tensile strength to increase by 380-400 MPa.
- the hardened springs then were subjected to fatigue testing. This was carried out by tightening the springs with an under-tension of 100 MPa and then compressing them with a tension of 900 MPa. This compression and release were repeated at a high frequency 20 million times for each spring or until rupture occured. Twenty springs made of each of the materials were tested. The results are given in Table 2, in which the springs la s , 2a s , and 3a s are made of wires manufactured conventionally, while the springs lb s , 2b s , and 3b s are made of cold drawn wires manufactured according to the invention. The table shows that the springs of the invention not in any single case were fatigued to fracture, while 20 %, 90 %, and 75 %, respectively of the reference springs were fatigued to fracture before 20 millions of oscillations had been performed.
Abstract
Description
Claims
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
DE29824794U DE29824794U1 (en) | 1997-12-17 | 1998-12-08 | Cold drawn wire and spring |
Applications Claiming Priority (3)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
SE9704753 | 1997-12-17 | ||
SE9704753A SE9704753L (en) | 1997-12-17 | 1997-12-17 | Ways to make cold drawn wire of ESR remelted stainless steel and cold drawn wire |
PCT/SE1998/002238 WO1999031282A1 (en) | 1997-12-17 | 1998-12-08 | Cold drawn wire and method for the manufacturing of such wire |
Publications (2)
Publication Number | Publication Date |
---|---|
EP1042516A1 true EP1042516A1 (en) | 2000-10-11 |
EP1042516B1 EP1042516B1 (en) | 2004-03-03 |
Family
ID=20409461
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
EP98963686A Expired - Lifetime EP1042516B1 (en) | 1997-12-17 | 1998-12-08 | Cold drawn wire and method for the manufacturing of such wire |
Country Status (11)
Country | Link |
---|---|
US (1) | US6383316B1 (en) |
EP (1) | EP1042516B1 (en) |
JP (1) | JP4334764B2 (en) |
KR (1) | KR100571438B1 (en) |
AT (2) | ATE260991T1 (en) |
AU (1) | AU1895799A (en) |
BR (1) | BR9813472A (en) |
DE (2) | DE1042516T1 (en) |
ES (1) | ES2170041T3 (en) |
SE (1) | SE9704753L (en) |
WO (1) | WO1999031282A1 (en) |
Families Citing this family (11)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
DE10110384A1 (en) * | 2001-03-03 | 2002-09-19 | Stahlwerk Ergste Westig Gmbh | Stainless steel wire |
US6692550B2 (en) * | 2002-03-28 | 2004-02-17 | General Electric Company | Fabrication of a high-strength steel article with inclusion control during melting |
US7094273B2 (en) | 2002-03-29 | 2006-08-22 | General Electric Company | Fabrication of a high-strength steel article with inclusion control during melting |
TW201028240A (en) * | 2009-01-23 | 2010-08-01 | jun-de Li | Composite bonding wire manufacturing method and product thereof |
IT1396294B1 (en) * | 2009-10-05 | 2012-11-16 | Gally S P A | SELF-LOCKING NUTS |
CN104745765B (en) * | 2015-03-26 | 2017-01-25 | 中天钢铁集团有限公司 | Smelting process of Cr-Mn series spring steel |
JP2020533490A (en) * | 2017-09-07 | 2020-11-19 | スズキ ガルフィタン アクチエボラグ | Methods for manufacturing cold drawn wire |
JP7049142B2 (en) * | 2018-03-15 | 2022-04-06 | 日鉄ステンレス株式会社 | Martensitic stainless steel sheet and its manufacturing method and spring members |
SE541925C2 (en) | 2018-04-26 | 2020-01-07 | Suzuki Garphyttan Ab | A stainless steel |
CN109680121B (en) * | 2019-01-15 | 2020-10-23 | 北京科技大学 | Reducing CaO-SiO content in deep-drawn cutting wires2-Al2O3Process for making steel from inclusions |
CN112846115A (en) * | 2020-12-31 | 2021-05-28 | 浦项(张家港)不锈钢股份有限公司 | Smelting and casting process of titanium-chromium-nickel-containing semi-austenite precipitation hardening stainless steel |
Family Cites Families (6)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
SE373387B (en) * | 1973-06-08 | 1975-02-03 | Sandvik Ab | PROCEDURE FOR MANUFACTURE OF BAND OR THREAD, EXV. ROUND FOR SPRING END |
AT343300B (en) * | 1975-02-25 | 1978-05-26 | Ver Edelstahlwerke Ag | METHOD FOR PRODUCING HOMOGENEOUS BLOCKS |
US4265679A (en) * | 1979-08-23 | 1981-05-05 | Kawasaki Steel Corporation | Process for producing stainless steels for spring having a high strength and an excellent fatigue resistance |
JPS60177139A (en) | 1984-02-23 | 1985-09-11 | Daido Steel Co Ltd | Manufacture of extremely clean steel |
DE3940438C1 (en) * | 1989-12-07 | 1991-05-23 | Vereinigte Schmiedewerke Gmbh, 4630 Bochum, De | |
JP3245781B2 (en) * | 1992-10-06 | 2002-01-15 | 大同特殊鋼株式会社 | Stainless steel for single wire drawing and its manufacturing method |
-
1997
- 1997-12-17 SE SE9704753A patent/SE9704753L/en not_active IP Right Cessation
-
1998
- 1998-12-08 DE DE1042516T patent/DE1042516T1/en active Pending
- 1998-12-08 JP JP2000539179A patent/JP4334764B2/en not_active Expired - Lifetime
- 1998-12-08 WO PCT/SE1998/002238 patent/WO1999031282A1/en active IP Right Grant
- 1998-12-08 US US09/581,658 patent/US6383316B1/en not_active Expired - Lifetime
- 1998-12-08 EP EP98963686A patent/EP1042516B1/en not_active Expired - Lifetime
- 1998-12-08 AU AU18957/99A patent/AU1895799A/en not_active Abandoned
- 1998-12-08 ES ES98963686T patent/ES2170041T3/en not_active Expired - Lifetime
- 1998-12-08 BR BR9813472-8A patent/BR9813472A/en not_active Application Discontinuation
- 1998-12-08 KR KR1020007006633A patent/KR100571438B1/en not_active IP Right Cessation
- 1998-12-08 AT AT98963686T patent/ATE260991T1/en active
- 1998-12-08 DE DE69822211T patent/DE69822211T2/en not_active Expired - Lifetime
-
2002
- 2002-06-27 AT AT0041602U patent/AT6041U1/en unknown
Non-Patent Citations (1)
Title |
---|
See references of WO9931282A1 * |
Also Published As
Publication number | Publication date |
---|---|
DE1042516T1 (en) | 2002-06-13 |
KR100571438B1 (en) | 2006-04-17 |
ES2170041T3 (en) | 2004-10-16 |
AT6041U1 (en) | 2003-03-25 |
WO1999031282A1 (en) | 1999-06-24 |
DE69822211D1 (en) | 2004-04-08 |
JP2002508443A (en) | 2002-03-19 |
KR20010024738A (en) | 2001-03-26 |
SE9704753D0 (en) | 1997-12-17 |
JP4334764B2 (en) | 2009-09-30 |
SE508814C2 (en) | 1998-11-09 |
AU1895799A (en) | 1999-07-05 |
ES2170041T1 (en) | 2002-08-01 |
EP1042516B1 (en) | 2004-03-03 |
ATE260991T1 (en) | 2004-03-15 |
US6383316B1 (en) | 2002-05-07 |
DE69822211T2 (en) | 2005-02-17 |
SE9704753L (en) | 1998-11-09 |
BR9813472A (en) | 2000-10-10 |
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